Semiconductor processing apparatus with a ceramic-comprising surface which exhibits fracture toughness and halogen plasma resistance

ABSTRACT

A solid solution-comprising ceramic article useful in semiconductor processing, which article may be in the form of a solid, bulk ceramic, or may be in the form of a substrate having a ceramic coating of the same composition as the bulk ceramic material on at least one outer surface. The ceramic article is resistant to erosion by halogen-containing plasmas and provides advantageous mechanical properties. The solid solution-comprising ceramic article is formed from a combination of yttrium oxide and zirconium oxide. The ceramic-comprising article includes ceramic which is formed from zirconium oxide at a molar concentration ranging from about 96 mole % to about 91 mole %, and yttrium oxide at a molar concentration ranging from about 4 mole % to about 9 mole %.

This application is a divisional application of U.S. application Ser. No. 13/986,040, filed on Mar. 25, 2013 entitled: “Semiconductor Processing Apparatus Comprising A Solid Solution Ceramic Formed From Yttrium Oxide, Zirconium Oxide, and Aluminum Oxide”, which issued as U.S. Pat. No. 9,051,219 on Jun. 9, 2015; which is a continuation application of U.S. application Ser. No. 13/199,521, filed on Aug. 31, 2011, entitled: “Semiconductor Processing Apparatus Comprising A Coating Formed From a Solid Solution of Yttrium Oxide and Zirconium Oxide”, which issued as U.S. Pat. No. 8,623,527 on Jan. 7, 2014; which is a divisional application of U.S. application Ser. No. 12/660,068, filed on Feb. 19, 2010, entitled: “Semiconductor Processing Apparatus Which is Formed From Yttrium Oxide and Zirconium Oxide to Produce a Solid Solution Ceramic Apparatus”, which issued as U.S. Pat. No. 8,034,734 on Oct. 11, 2011; which is a continuation application of U.S. application Ser. No. 11/796,210, filed on Apr. 27, 2007, entitled: “Method of Reducing the Erosion Rate of Semiconductor Processing Apparatus Exposed to Halogen-Containing Plasmas”, which has gone abandoned.

The present application is related to a series of applications filed by various inventors of the present application, many of the applications relate to the use of a yttrium-oxide comprising ceramic in the form of a coating, to provide a plasma-resistant surface which is useful in semiconductor processing applications. The applications include U.S. application Ser. No. 10/075,967 of Sun et al., filed Feb. 14, 2002, titled: “Yttrium Oxide Based Surface Coating For Semiconductor IC Processing Vacuum Chambers”, which issued as U.S. Pat. No. 6,776,873 on Aug. 17, 2004; U.S. application Ser. No. 10/898,113 of Sun et al., filed Jul. 22, 2004, titled: “Clean Dense Yttrium Oxide Coating Protecting Semiconductor Apparatus”, which is currently pending; and U.S. application Ser. No. 10/918,232 of Sun et al., filed Aug. 13, 2004, titled: “Gas Distribution Plate Fabricated From A Solid Yttrium Oxide-Comprising Substrate”, which is currently pending. Additional related applications filed, which are a divisional and a continuation application of above-listed applications, include: U.S. application Ser. No. 11/595,484 of Wang et al., filed Nov. 10, 2006, titled: “Cleaning Method Used In Removing Contaminants From The Surface Of An Oxide or Fluoride Comprising a Group III Metal”, which is currently pending, and which is a divisional application of U.S. application Ser. No. 10/898,113; and U.S. application Ser. No. 11/592,905 of Wang et al., filed Nov. 3, 2006, titled: “Cleaning Method Used In Removing Contaminants From A Solid Yttrium Oxide-Containing Substrate”, which is currently pending, and which is a continuation application of U.S. application Ser. No. 10/918,232. The subject matter of all of these patents and applications is hereby incorporated by reference.

BACKGROUND

1. Field

The present invention relates to a specialized yttrium oxide comprising solid solution ceramic which is highly resistant to plasmas in general, particularly resistant to corrosive plasmas of the kind used in the etching of semiconductor substrates.

2. Description of the Background Art

This section describes background subject matter related to the disclosed embodiments of the present invention. There is no intention, either express or implied, that the background art discussed in this section legally constitutes prior art.

Corrosion (including erosion) resistance is a critical property for apparatus components and liners used in semiconductor processing chambers, where corrosive environments are present. Example of corrosive plasma environments include plasmas used for cleaning of processing apparatus and plasmas used to etch semiconductor substrates. Plasmas used for plasma-enhanced chemical vapor deposition processes often tend to be corrosive as well. This is especially true where high-energy plasma is present and combined with chemical reactivity to act upon the surface of components present in the environment. The reduced chemical reactivity of an apparatus component surface or of a liner surface is also an important property when corrosive gases alone are in contact with processing apparatus surfaces.

Process chambers and component apparatus present within processing chambers which are used in the fabrication of electronic devices and micro-electro-mechanical structures (MEMS) are frequently constructed from aluminum and aluminum alloys. Surfaces of a process chamber and component apparatus present within the chamber are frequently anodized to provide a degree of protection from the corrosive environment. However, the integrity of the anodization layer may be deteriorated by impurities in the aluminum or aluminum alloy, so that corrosion begins to occur early, shortening the life span of the protective coating. Ceramic coatings of various compositions have been used in place of the aluminum oxide layer mentioned above, and have been used over the surface of the anodized layer to improve the protection of the underlying aluminum-based materials. However, current materials used for protective layers deteriorate over time and eventually leave the aluminum alloy subject to attack by the plasma, even though the life span of the protective layer is extended over that of anodized aluminum.

Yttrium oxide is a ceramic material which has shown considerable promise in the protection of aluminum and aluminum alloy surfaces which are exposed to fluorine-containing plasmas of the kind used in the fabrication of semiconductor devices. A yttrium oxide coating has been used and applied over an anodized surface of a high purity aluminum alloy process chamber surface, or a process component surface, to produce excellent corrosion protection (e.g. U.S. Pat. No. 6,776,873 to Sun et al., mentioned above). In one application, the '873 patent provides a processing chamber component resistant to a plasma including fluorine and oxygen species. The processing chamber component typically comprises: a high purity aluminum substrate, where particulates formed from mobile impurities present in the aluminum are carefully controlled to have a particular size distribution; an anodized coating on a surface of the high purity aluminum substrate; and, a protective coating comprising yttrium oxide overlying the anodized coating. The protective coating may include aluminum oxide up to about 10% by weight, and typically comprises 99.95% by weight or greater yttrium oxide. The protective coating is typically applied using a method such as spray coating, chemical vapor deposition, or physical vapor deposition.

U.S. Pat. No. 5,798,016, to Oehrlein et al., issued Aug. 25, 1998, describes the use of aluminum oxide as a coating layer for chamber walls or as a coating layer for a chamber liner. The Oehrlein et al. reference further discloses that since aluminum is reactive with a number of plasmas, it is recommended that “aluminum oxide or a coating thereof be disposed on the liner or chamber walls”, because aluminum oxide tends to be chemically inert. In addition, a protective coating may be applied over the surfaces of the liner and/or chamber walls. Examples which are given include Al₂O₃, Sc₂O₃, or Y₂O₃.

U.S. Patent Application Publication No. US 2001/0003271A1, of Otsuki, published Jun. 14, 2001, and subsequently abandoned, discloses a film of Al₂O₃, or Al₂O₃ and Y₂O₃, formed on an inner wall surface of the chamber and on those exposed surfaces of the members within the chamber which require a high corrosion resistance and insulating property. An example is given of a processing chamber where a base material of the chamber may be a ceramic material (Al₂O₃, SiO₂, AlN, etc.), aluminum, or stainless steel, or other metal or metal alloy, which has a sprayed film over the base material. The film may be made of a compound of a III-B element of the periodic table, such as Y₂O₃ The film may substantially comprise Al₂O3 and Y₂O₃. A sprayed film of yttrium-aluminum-garnet (YAG) is also mentioned. The sprayed film thickness is said to range from 50 μm to 300 μm.

In another application, a ceramic composition of matter comprising a ceramic compound (e.g. Al₂O₃) and an oxide of a Group IIIB metal (e.g. Y₂O₃) has been used for a dielectric window of a reactor chamber where substrates are processed in a plasma of a processing gas (e.g. U.S. Pat. No. 6,352,611, to Han et al., issued Mar. 5, 2002). The ceramic compound may be selected from silicon carbide, silicon nitride, boron carbide, boron nitride, aluminum nitride, aluminum oxide, and mixtures thereof; however, aluminum oxide is said to be available in a pure form which does not outgas. The Group IIIB metal may be selected from the group consisting of scandium, yttrium, the cerium subgroup, and the yttrium subgroup; however, yttrium is preferred, with the oxide being yttrium oxide. The preferred process for forming or producing the dielectric member is by thermal processing of a powdered raw mixture comprising the ceramic compound, the oxide of a Group IIIB metal, a suitable additive agent, and a suitable binder agent.

In another application, a protective coating for a semiconductor processing apparatus component is described. The protective coating comprises aluminum or an aluminum alloy, where the coating includes a material selected from, for example, but not limited to: yttrium-aluminum-garnet (YAG); an oxide of an element selected from the group consisting of Y, Sc, La, Ce, Eu, and Dy; a fluoride of an element selected from the group consisting of Y, Sc, La, Ce, Eu, and Dy; and combinations thereof is used (e.g. U.S. patent application Ser. No. 10/898,113 of Sun et al., filed Jul. 22, 2004, and entitled “Clean, Dense Yttrium Oxide Coating Protecting Semiconductor Apparatus”, mentioned above). The coating is applied to a substrate surface by thermal/flame spraying, plasma spraying, sputtering, or chemical vapor deposition (CVD). The coating is placed in compression by applying the coating at a substrate surface temperature of at least about 150-200° C.

The kinds of protective coatings described above have been used to protect exposed surfaces of a plasma source gas distribution plate of the kind used in semiconductor and MEMS processing apparatus. However, due to the concentration of reactive species which are present at the surface of the gas distribution plate, the lifetime of the gas distribution plate has typically been limited, from about 8 processing days to about 80 processing days, depending on the corrosivity of the plasma created in the processing chamber. To increase the lifetime of a component such as a gas distribution plate, a gas distribution plate was fabricated from a solid yttrium oxide-comprising substrate, as described in U.S. application Ser. No. 10/918,232 of Sun et al., mentioned above. The solid yttrium oxide-comprising substrate contains up to about 10% aluminum oxide in some instances. The solid yttrium oxide-comprising substrate typically comprises about 99.99% yttrium oxide.

As device geometry continues to shrink, the on-wafer defect requirements become more stringent, as particulate generation from apparatus within the processing chamber increases in importance. For plasma dry etch chambers running various halogen, oxygen, and nitrogen chemistries, such as F, Cl, Br, O, N, and various combinations thereof, for example, the selection of the material used for apparatus components and chamber liners becomes more critical. The materials with good plasma resistance performance (which also have adequate mechanical, electrical and thermal properties), can reduce particle generation, metal contamination, and provide prolonged component life. This translates to low costs of manufacturing, reduced wafer defects, increased lifetime, and increased mean time between cleaning. Ceramic materials which have been used in such applications include Al₂O₃, AlN, and SiC. However, the plasma resistance properties of these ceramic materials is not adequate in many instances, particularly when a fluorine plasma source gas is involved. The recent introduction of Y₂O₃ ceramic shows improved plasma resistance properties, but this material generally exhibits weak mechanical properties that limits its applications for general use in semiconductor processing components, processing kits, and chamber liners.

SUMMARY

Semiconductor processing conditions expose semiconductor processing apparatus, such as the interior of processing chambers and the surfaces of components within the processing chambers, to a variety of chemical reagents and plasma ions which attack processing apparatus surfaces. The effect of the attack on an apparatus surface is frequently referred to as erosion of the apparatus surface. It is possible to reduce the erosion rate by selecting a particular material composition for the apparatus surfaces. A protective material may be applied as a coating over the apparatus surface; however, this may not be the best solution to avoiding erosion. The coating is constantly getting thinner (eroding) during a plasma etch, and there is an increased risk that the substrate beneath the coating will be attacked by the plasma penetrating the coating layer. The coating layer may flake off during plasma processing due to residual stress. While such problems will be significantly reduced by using a coating of the erosion-resistant materials described in embodiments herein, in many instances it may be advantageous to form an entire apparatus component from the erosion-resistant materials. However, frequently the materials which are more erosion-resistant are more crystalline, and an improvement in erosion resistance comes at a cost, in the form of decreased mechanical properties (such as ductility) of the apparatus. Ceramic materials which are formed from an oxide of a Group IIIA, IIIB, IVB and VB element, or combinations thereof, have been demonstrated to provide erosion resistance to halogen-comprising plasmas. Embodiments of the present invention pertain to reducing the erosion rate of a ceramic material, typically comprising a Group IIIA, IIIB, IVB, or a Group IVB element, or combinations thereof, while maintaining acceptable mechanical properties or improving mechanical properties of the component parts made of the ceramic material.

In one embodiment, sintered ceramics are formed which contain a single solid solution phase or which are multi-phase, such as two phase and three phase. The multi-phase ceramics typically contain a yttrium aluminate phase and one or two solid solution phases formed from yttrium oxide, zirconium oxide and/or rare earth oxides. The sintered ceramic has been evaluated under various plasma processing conditions to determine erosion resistance. The materials which were erosion tested were also tested for mechanical properties. For example, ceramic materials formed from starting compositions in which the Y₂O₃, yttrium oxide, molar concentration ranges from about 50 mole % to about 75 mole %; the ZrO₂, zirconium oxide, molar concentration ranges from about 10 mole % to about 30 mole %; and, the Al₂O₃, aluminum oxide, molar concentration ranges from about 10 mole % to about 30 mole % provide excellent erosion resistance to halogen-containing plasmas while providing advanced mechanical properties which enable handling of solid ceramic processing components with less concern about damage to a component. In many embodiments, a starting composition for the ceramic materials may be one that comprises Y₂O₃ molar concentration ranges from about 55 mole % to about 65 mole %, ZrO₂ molar concentration ranges from about 15 mole % to about 25 mole %, and Al₂O₃ molar concentration ranges from about 10 mole % to about 25 mole %. When the erosion rate is of great concern, the starting material concentration of the ceramic material may be one that comprises Y₂O₃ molar concentration ranges from about 55 mole % to about 65 mole %, the ZrO₂ molar concentration ranges from about 20 mole % to about 25 mole % and the Al₂O₃ molar concentration 10 mole % to about 15 mole %. In one embodiment, to produce a solid apparatus component, these starting material formulations are compacted into a pelletized form and are sintered using a method selected from pressureless sintering, hot-press sintering (HP), or hot isostatic press sintering (HIP). These sintering techniques are well known in the art.

In other embodiments, the starting material compositions listed above may be used to form a ceramic coating over the surface of a variety of metal and ceramic substrates, including, but not limited to, aluminum, aluminum alloy, stainless steel, alumina, aluminum nitride and quartz, using a technique well known in the art, such as plasma spraying, for example and not by way of limitation. Typically the aluminum alloy used is a high purity aluminum alloy of the kind described in U.S. Pat. No. 6,776,873 to Sun et al., mentioned above. However, with the improved mechanical properties which have been obtained, it is recommended that solid ceramic apparatus components be used when possible, to avoid the eventual failure of the apparatus to function properly due to interfacial problems between the coating and the underlying substrate, or to prevent a sudden failure of plasma resistance due to the coating layer flaking off, or to prevent plasma penetration of the coating layer through defects which may be exposed from within the coating layer as the coating layer becomes thinner due to erosion.

The addition of zirconium oxide powder to yttrium oxide powder at a concentration of zirconium oxide, ranging from about 0.1 mole % to about 65 mole %, after consolidation by conventional ceramic processing, provides a single solid solution with a cubic yttria crystal structure phase or a cubic fluorite-type crystal structure phase, or provides a mixed solid solution of cubic yttria crystal structure phase and cubic fluorite-type crystal structure phase. For the cubic yttria crystal structure, the cell parameter of the solid solution is smaller than that of the pure cubic yttrium oxide crystalline structure, due to the formation of yttrium vacancy. For the cubic fluorite-type crystal structure, the cell parameter of the solid solution is smaller than that of the pure cubic fluorite-type structure, due to the formation of oxygen vacancy. The smaller cell parameter improves the plasma resistance properties of the solid solution of zirconium oxide in yttrium oxide. For example, the erosion rate of a pure solid yttrium oxide ceramic in a CF₄/CHF₃ plasma is about 0.3 μm/hr. The erosion rate (the rate at which a surface is removed in μm (of thickness)/hr) of a solid ceramic of about 69 mole % yttrium oxide and about 31 mole % zirconium oxide is about 0.1 μm/hr, a 3 times slower erosion rate than pure solid yttrium oxide. This unexpected decrease in erosion rate extends the lifetime of a process chamber liner or an internal apparatus component within the process chamber, so that the replacement frequency for such apparatus is reduced, reducing apparatus down time; and, the particle and metal contamination level generated during a plasma process is reduced, enabling a device fabrication with ever shrinking geometry with reduced overall cost of the processing apparatus per wafer processed, on the average.

While the 0.1 μm/hr erosion rate for the zirconium oxide-containing yttrium oxide solid solution is surprisingly better than that of yttrium oxide at 0.3 μm/hr, and considerably better than of a solid aluminum oxide ceramic at 1.44 μm/hr in the CF₄/CHF₃ plasma, the mechanical properties of the zirconium oxide-containing yttrium oxide solid solution illustrate that an improvement in flexural strength and fracture toughness would be helpful.

In one embodiment, the flexural strength and fracture toughness of the zirconium oxide-containing yttrium oxide solid solution are achieved, by adding various amounts of aluminum oxide to the formula for the solid solution ceramic to form an additional yttrium aluminate phase. The mixture of oxides was pelletized by unidirectional mechanical pressing or cold isostatic pressing of a granular powder formed by spray drying, in combination with a typical content of binders. The green body was then pressureless sintered using techniques generally known in the art. The addition of 10 mole % to 30 mole % of alumina significantly improved the mechanical properties of the sintered ceramic composition in terms of flexural strength and fracture toughness, as discussed subsequently herein. This surprising change in mechanical properties, which indicates that fabricated parts could be handled with less risk of fracture, was achieved with minimal effect on the plasma erosion rate of the ceramic material. For example, the erosion rate of the ceramic containing 69 mole % yttrium oxide and 31 mole % zirconium oxide, after exposure to a plasma containing CF₄ and CHF₃, was about 0.1 μm/hr. For the ceramic containing about 14 mole % aluminum oxide, the erosion rate after exposure to the same plasma was also about 0.1 μm/hr. For the ceramic containing about 25 mole % aluminum oxide, the erosion rate after exposure to the same plasma was about 0.2 μm/hr. The relationship between aluminum oxide content, increase in flexural strength, and increase in erosion rate is not a linear relationship. However, one of skill in the art can optimize the formula with minimal experimentation, in view of the information provided herein.

As an alternative to adding aluminum oxide to a multi phase metal stable composition containing yttrium oxide and zirconium oxide, it is possible to add HfO₂, hafnium oxide; Sc₂O₃, scandium oxide; Nd₂O₃, neodymium oxide; Nb₂O₅, niobium oxide; Sm₂O₃, samarium oxide; Yb₂O₃, ytterbium oxide; Er₂O₃, erbium oxide; Ce₂O₃ (or CeO₂), cerium oxide, or combinations thereof. In the instance where one of these alternative oxides is used, the concentration of the oxide in the starting material formulation ranges from about 0.1 mole % to about 90 mole %, and typically ranges from about 10 mole % to about 30 mole %.

After mixing of at least one of the alternative oxides listed above with the Y₂O₃ and ZrO₂ powders used to form a solid solution, the combination of powders was compacted by unidirectionally mechanical pressing or cold isostatic pressing of the granular powder formed by spray drying with a typical content of binders. The green body was then pressureless sintered using techniques known in the art. Upon cooling of the sintered body, a single phase or two phase solid solution forms, where the solid solution is a “multi-element-doped” solid solution. One solid solution exhibits a cubic yttria crystal structure, and another solid solution exhibits the cubic fluorite-type crystal structure. The solid solution has excellent plasma resistance, typically better erosion resistance than that of the aluminum oxide-comprising solid solutions discussed herein. However, the mechanical properties of the yttria-zirconia-alumina system are somewhat better. All of these multi-doped solid solutions exhibit excellent plasma erosion resistance and improved mechanical properties in comparison with previously known yttrium oxide-zirconium oxide solid solutions.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 A shows a photomicrograph of the as-sintered surface of a solid yttrium oxide ceramic at a magnification of 1,000 times.

FIG. 1B shows a photomicrograph of the as-sintered surface of a solid solution ceramic substrate formed from 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide, at a magnification of 1,000 times.

FIG. 1C shows a photomicrograph of the as-sintered surface of a solid solution ceramic substrate formed from 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide, at a magnification of 1,000 times.

FIG. 2A shows a photomicrograph of the surface of a solid yttrium oxide ceramic after a test etch using the processing plasmas and times typically used to etch the various layers of a contact via feature in a semiconductor device. The magnification is 1,000 times.

FIG. 2B shows a photomicrograph of the surface of a solid solution ceramic formed from 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide after a test etch using the processing plasmas and times typically used to etch the various layers of a contact via feature in a semiconductor device. The magnification is 1,000 times.

FIG. 2C shows a photomicrograph of the surface of a solid solution ceramic formed from 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide after a test etch using the processing plasmas and times typically used to etch the various layers of a contact via feature in a semiconductor device. The magnification is 1,000 times.

FIG. 3A shows a photomicrograph of the post-etch ceramic of FIG. 2A, but at a magnification of 5,000 times.

FIG. 3B shows a photomicrograph of the post-etch ceramic of FIG. 2B, but at a magnification of 5,000 times.

FIG. 3C shows a photomicrograph of the post-etch ceramic of FIG. 2C, but at a magnification of 5,000 times.

FIG. 4A shows a photomicrograph of the as-sintered surface of a solid solution ceramic formed from 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide, at a magnification of 2,000 times.

FIG. 4B shows a photomicrograph of the surface of the solid solution ceramic shown in FIG. 4A, after exposure of the test coupon to a trench etch process of the kind described herein. The magnification is 2,000 times.

FIG. 4C shows a photomicrograph of the as sintered surface of a solid solution ceramic formed from 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide, at a magnification of 2,000 times.

FIG. 4D shows a photomicrograph of the surface of the solid solution ceramic shown in FIG. 4C, after exposure of the test coupon to a trench etch process of the kind described herein. The magnification is 2,000 times.

FIG. 5A shows a photomicrograph of a solid solution ceramic formed from 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide after exposure of the test coupon to a metal etch process of the kind described herein. The magnification is 5,000 times.

FIG. 5B shows a photomicrograph of a solid solution ceramic formed from 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide after exposure of the test coupon to an etch by a CF₄/CHF₃ plasma. The magnification of 5,000 times.

DETAILED DESCRIPTION OF EXEMPLARY EMBODIMENTS

As a preface to the detailed description, it should be noted that, as used in this specification and the appended claims, the singular forms “a”, “an”, and “the” include plural referents, unless the context clearly dictates otherwise.

When the word “about” is used herein, this is intended to mean that the nominal value presented is precise within ±10%.

Bulk yttrium oxide has been shown to have very good corrosion resistance upon exposure to fluorine plasma and other corrosive plasmas which are typically used in semiconductor manufacturing processes (such as etch processes and chemical vapor deposition processes). However, pure crystalline yttrium oxide, while offering very good corrosion resistance to various etchant plasmas, does not offer good mechanical properties in terms of flexural strength and fracture toughness, for example. To improve the overall performance and handling capabilities of semiconductor component parts and liners, there is a need to improve the mechanical properties from those available in pure crystalline yttrium oxide. To obtain the improvement in mechanical properties, it is necessary to form an alloy of yttrium oxide with a compatible oxide. The improvement in mechanical properties needed to be accomplished without harming the very good plasma erosion properties of the pure yttrium oxide.

In consideration of the Gibbs Formation Free Energy of various ceramic materials which might be compatible with yttrium oxide, we determined that it is more difficult to form fluorides than oxides for yttrium and aluminum elements, so that yttrium oxide and aluminum oxide are expected to provide good resistance to a fluorine-containing plasma. The Gibbs Formation Free Energy of zirconium fluoride is similar to that for yttrium fluoride. Further, in a homogeneous amorphous oxyfluoride, or a glass-ceramic composite oxyfluoride, increasing the zirconium fluoride content can decrease the free energy of the final oxyfluoride to make it more stable.

Example Embodiments:

Example One: Etch Plasma Process Conditions for Erosion Rate Testing

Tables One-Three, below, provides the etch plasma compositions and etch plasma processing conditions which were used for evaluation of a series of test coupon materials. There were three basic different sets of etch plasma conditions which were used for the erosion rate testing: 1) Trench etching, where the etch plasma source gas and etch process conditions were representative of etching a trench feature size beyond 65 nm technology, i.e. smaller than 65 nm, into a multilayered semiconductor substrate. Such a substrate typically includes an antireflective coating (ARC or BARC) layer, an organic or inorganic dielectric layer, a metal layer, and an etch stop layer. Contact Via etching, where the etch plasma source gas and etch process conditions were representative of etching a contact via having an aspect ratio of about 30 in production and 40 plus in the developed device substrate, and having a diameter of beyond 65 nm technology into a multilayered semiconductor substrate including a buried ARC (BARC) layer, a dielectric layer and a stop layer; and 3) Metal etching, here the etch plasma source gas and etch process conditions were representative of etching an overlying titanium nitride hard mask and an aluminum layer, where the etch plasma source gas and etch process conditions are beyond 65 nm technology.

The trench etching process and the contact via etching process were carried out in the ENABLER′ processing system, and the metal etching process was carried out in the DPS™ processing system, all available from Applied Materials, Inc. of Santa Clara, Calif.

TABLE ONE Process Conditions for Trench Etch Erosion Rate Test Trench Etch Plasma Source Subr Bias Subr Simulation CF₄ * O₂ * CHF₃ * N₂ * Ar * Power¹ Pr² Power ³ Temp ⁴ Time ⁵ Etch Step One 150 30 300 1,000   40 35 Etch Step Two 400 1200 220 400 40 40 Etch Step Three 175 15 1500 150 500 40 39 Etch Step Four 500  100  10 200 40 55 * All gas flow rates are in sccm. ¹Plasma Source Power in W. ²Pressure in mTorr. ³ Substrate Bias Power in W. ⁴ Substrate Temperature in ° C. ⁵ Time in seconds.

TABLE TWO Process Conditions for Via Etch Erosion Rate Test Via Etch Simulation CF₄ * C₄F₆ * CHF₃ * CH₂F₂ * Ar * O₂ * N₂ * Etch Step 80 80 One Etch Step 28 15 20 500 31 Two Etch Step 40 650 30 Three Etch Step 200 Four Etch Step 500 Five Plasma Substrate Via Etch Source Bias Substrate Simulation Power¹ Pr² Power³ Temp⁴ Time⁵ Etch Step 80 400 40 50 One Etch Step 400 30 1700 40 60 Two Etch Step 30 1700 40 60 Three Etch Step 1000 50 100 40 45 Four * All gas flow rates are in sccm. ¹Plasma Source Power in W. ²Pressure in mTorr. ³Substrate Bias Power in W. ⁴Substrate Temperature in ° C. ⁵Time in seconds.

TABLE THREE Process Conditions for Metal Etch Erosion Rate Test Metal Etch Plasma Source Subr Bias Prc Subr Simul. Cl₂ * BCl₃ * C₂H₄ * Ar * CHF₃ * N₂ * Power ¹ Power ² Pr ³ Temp ⁴ Time ⁵ Etch Step One 60 3 20 1000 100 8 40 30 Etch Step Two 25 40 10 5 500 150 10 40 18 Etch Step Three 60 40 20 700 120 18 40 30 Etch Step Four 60 40 3 1000 200 8 40 23 Etch Step Five 30 60 5 50 5 800 170 6 40 15 * All gas flow rates are in sccm. ¹ Plasma Source Power in W. ² Substrate Bias Power in W. ³ Pressure in mTorr. ⁴ Substrate Temperature in ° C. ⁵ Time in seconds.

Example Two: Comparative Relative Erosion Rates of Various Ceramic Materials Compared with Aluminum Oxide

Aluminum oxide has frequently been used as a protective layer or liner when a semiconductor process makes use of an etchant plasma. Using aluminum oxide as the base comparative material, we determined the relative etch rates, in a Trench Etch (CF₄/CHF₃) environment. With aluminum oxide having a relative erosion rate of 1, we found that the relative erosion rate of quartz was about 2.2 times that of aluminum oxide. The relative erosion rate of silicon carbide was about 1.6 times that of aluminum oxide. The relative erosion rate of zirconia was about 0.8 times that of aluminum oxide. The relative erosion rate of pure yttrium oxide was about 0.19 times that of aluminum oxide. The relative erosion rate of a yttrium oxide, zirconium oxide, aluminum oxide ceramic composite, formed from 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide was about 0.2 times that of aluminum oxide. The relative erosion rate of a yttrium oxide, zirconium oxide, aluminum oxide ceramic composite, formed from 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide was about 0.05 times that of aluminum oxide.

Example Three: Measured Erosion Rates for Trench Etching Process

With reference to the trench etching method described above, the sample substrate test coupon erosion rates measured were as follows. The erosion rate of aluminum oxide was 1.1 μm/hr. The erosion rate of bulk yttrium oxide was 0.3 μm/hr. The erosion rate of a the a yttrium oxide, zirconium oxide, aluminum oxide ceramic composite, formed from 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide was 0.1 μm/hr. The erosion rate of a yttrium oxide, zirconium oxide, aluminum oxide ceramic composite, formed from 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide was 0.07 μm/hr.

Example Four: Measured Erosion Rates for Via Etching Process

With reference to the via etching method described above, the sample substrate test coupon erosion rates measured were as follows. The erosion rate of aluminum oxide was not measured. The erosion rate of bulk yttrium oxide was 0.16 μm/hr. The erosion rate of a the a yttrium oxide, zirconium oxide, aluminum oxide solid solution, formed from 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide was 0.21 μm/hr. The erosion rate of a yttrium oxide, zirconium oxide, aluminum oxide solid solution, formed from 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide was 0.22 μm/hr.

Example Five: Measured Erosion Rates for Metal Etching Process

With reference to the metal etching method described above, the sample substrate test coupon erosion rates measured were as follows. The erosion rate of aluminum oxide was 4.10 μm/hr. The erosion rate for bulk yttrium oxide was 0.14 μm/hr. The erosion rate of a the a yttrium oxide, zirconium oxide, aluminum oxide ceramic composite, formed from 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide was 0.10 μm/hr. The erosion rate of a yttrium oxide, zirconium oxide, aluminum oxide ceramic composite, formed from 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide was 0.18 μm/hr.

Example Six: Photomicrographs of Yttrium-Oxide-Based Ceramics after Exposure to a Via Etch Process

FIGS. 1A through 1C show photomicrographs of the surface of a sintered yttrium-oxide-containing ceramic composite prior to exposure to the via etch process described herein. The yttrium-oxide-containing ceramic composites include: 1) yttrium oxide-zirconium oxide solid solution; and 2) yttrium aluminate, when the composition was yttrium oxide 100 parts by weight, zirconium oxide 20 parts by weight, and aluminum oxide 10 parts by weight. (This composition is the same as 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide); and 3) yttrium oxide-zirconium oxide-aluminum oxide solid solution, when the composition from which the solid solution was formed was yttrium oxide 100 parts by weight, zirconium oxide 20 parts by weight, and aluminum oxide 20 parts by weight. (This composition is the same as 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide). All of the photomicrographs are at a magnification of 1,000 times.

FIGS. 2A through 2C show photomicrographs of the sintered yttrium-oxide-containing ceramic composite subsequent to exposure to the via etch process described herein. The yttrium-oxide-containing ceramic composites include: 1) yttrium oxide-zirconium oxide solid solution; and 2) yttrium aluminate, when the composition was yttrium oxide 100 parts by weight, zirconium oxide 20 parts by weight, and aluminum oxide 10 parts by weight (This composition is the same as 63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide); or when the composition was yttrium oxide 100 parts by weight, zirconium oxide 20 parts by weight, and aluminum oxide 20 parts by weight (This composition is the same as 55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide). All of the photomicrographs are at a magnification of 1,000 times.

The surface roughness of the bulk yttrium oxide shown in FIG. 2A has increased in roughness substantially. However, the overall surface roughness appears to be less than that of the zirconium oxide and aluminum oxide containing sample coupons. The surface roughness of the solid solution shown in FIG. 2B, which contains 10 parts by weight aluminum oxide appears to have hills and valleys which are flatter than the hills and valleys of the solid solution shown in FIG. 2C, which contains the 20 parts by weight of aluminum oxide. However, the hills and valleys on the 10 parts by weight aluminum oxide sample coupon shown in FIG. 2B have more pitting on the surface than in the 20 parts by weight sample coupon shown in FIG. 2C.

FIGS. 3A through 3C show photomicrographs which correspond with FIGS. 2A through 2C, respectively, but are at a magnification of 5,000 times. Looking at the surface of the bulk yttrium oxide sample coupon shown in FIG. 3A, the surface is relatively smooth but does show some evidence of small pits. The FIG. 3B solid solution formed from yttrium oxide 100 parts by weight, zirconium oxide 20 parts by weight, and aluminum oxide 10 parts by weight also shows some small scale pitting present on the rougher surface shown in FIG. 2B. The FIG. 3C solid solution formed from yttrium oxide 100 parts by weight, zirconium oxide 20 parts by weight, and aluminum oxide 20 parts by weigh shows negligible small scale pitting.

Looking at the erosion rates for the three test coupons, it appears that the 1,000 times magnification for the post-etch coupons shows better surface characteristics related to the erosion rates of the coupons. The erosion rates were 0.16 μm/hr for the solid yttrium oxide shown in FIG. 2A; 0.22 μm/hr for the solid solution of yttrium oxide-zirconium oxide-aluminum oxide which contained 10 parts by weight aluminum oxide; and 0.21 μm/hr for the solid solution of yttrium oxide-zirconium oxide-aluminum oxide which contained 20 parts by weight aluminum oxide.

Example Seven: Photomicrographs of Yttrium-Oxide-Containing Substrates after Exposure to a Trench Etch Process

FIG. 4A shows a photomicrograph of the as-sintered surface of a solid solution ceramic composite containing 100 parts by weight yttrium oxide, 20 parts by weight aluminum oxide, and 10 parts by weight aluminum oxide (63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide), at a magnification of 2,000 times. FIG. 4B shows a photomicrograph of the surface of the solid ceramic composite of FIG. 4A after etching by a trench etch process of the kind shown herein. Both photomicrographs are at a magnification of 2,000. The post-etched surface appears to be flat and relatively homogeneous. This combination of photographs suggests that after fabrication of an apparatus such as a chamber liner or a component part, it may be advisable to “season” the part by exposing it to an exemplary plasma etch process prior to introducing the apparatus into a semiconductor device production process. The erosion rate for the solid solution ceramic composite containing the 10 parts by weight of aluminum oxide, after exposure to the trench etch process, was about 0.08 μm/hr.

FIG. 4C shows a photomicrograph of the as-sintered surface of a solid solution ceramic composite containing 100 parts by weight yttrium oxide, 20 parts by weight aluminum oxide, and 20 parts by weight aluminum oxide (55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide). FIG. 4D shows a photomicrograph of the surface of the solid solution ceramic composite of FIG. 4C after etching by a trench etch process of the kind shown herein. Both photomicrographs are at a magnification of 2,000. The post-etched surface appears to be flat and relatively homogeneous. This combination of photographs suggests the same seasoning process described above for newly fabricated apparatus. The erosion rate of the solid solution ceramic composite containing the 20 parts by weight of aluminum oxide, after exposure to the trench etch process, was about 0.07 μm/hr.

Example Eight: Photomicrographs of Yttrium-Oxide-Containing Ceramic Composites after Exposure to a Metal Etch Process

FIG. 5A shows a photomicrograph of a two phase solid solution ceramic composite formed from 100 parts by weight of yttrium oxide, 20 parts by weight of zirconium oxide and 10 parts by weight of aluminum oxide (63 mole % yttrium oxide, 23 mole % zirconium oxide, and 14 mole % aluminum oxide) after exposure of the test coupon to a metal etch process of the kind described herein. The magnification is 5,000 times. FIG. 5B shows a photomicrograph of a two phase solid solution ceramic composite formed from 100 parts by weight of yttrium oxide, 20 parts by weight of zirconium oxide, and 10 parts by weight of aluminum oxide (55 mole % yttrium oxide, 20 mole % zirconium oxide, and 25 mole % aluminum oxide) after exposure of the test coupon to a metal etch process of the kind described herein. The magnification is 5,000 times. A comparison of these two photomicrographs shows that the two phase solid solution containing the higher content of aluminum oxide has an increased amount of the darker phase, which is yttrium aluminate. The erosion rate of the two phase solid solution ceramic composites containing the 10 parts by weight of aluminum oxide, after exposure to the trench etch process, was about 0.18 μm/hr, while the erosion rate of the two phase solid solution ceramic composite containing the 20 parts by weight of aluminum oxide, after exposure to the trench process was about 0.10 μm/hr.

Example Nine: Relative Physical and Mechanical Properties Of Yttrium-Oxide-Containing Substrates

Table Four below shows comparative physical and mechanical properties for the bulk, pure yttrium oxide ceramic and for various yttrium-oxide containing solid solution ceramics.

TABLE FOUR 100 Y₂O₃ 100 Y₂O₃ 100 ZrO2 100 Y₂O3 20 ZrO₂ 20 ZrO2 Material Starting 3 Y₂O₃ 20 ZrO₂ 10 Al₂O₃ 20 Al₂O₃ Composition Y₂O₃ Al₂O₃ parts by weight parts by weight. parts by weight parts by weight Flexural Strength 100-150 400 1200 ± 100 137 215 172 (MPa) Vickers Hardness 5.7 17.2 11.9 9.3 9.4 9.6 (5 Kgf)(GPa) Young's Modulus 140-170 380 373 190 190 202 (GPa) Fracture Toughness 1.0-1.3 3.5 10.9 1.3 1.6 1.7 (Mpa · m^(1/2)) Thermal Conductivity 13.7  33 2.9 4.7 3.5 (W/m/° K) Thermal Shock Resistance 130-200 200 130-200 150-200 (ΔT) ° C. Thermal Expansion × 10⁻⁶/ 7.2 7.7 9.4 9.0 8.5 K (20-900° C.) Dielectric Constant 12.3-13   9.9 — 15.0 15.5 (20° C. 13.56 MHZ) Dielectric Loss Tangent × <20    0.5 — <20 <20 — 10⁻⁴ (20° C. 13.56 MHZ) Volume Resistivity 10¹²-10¹³ 10¹⁵ — 10¹¹ 10¹⁶-10²² — at RT (Ω · cm) Density  4.92 3.95 5.89 5.19 4.90 4.86 (g/cm³) Mean Grain Size 10-25 — 0.5-1.0 5-10 3-6 3-6 (μm) Phase Y₂O₃ Al₂O₂ Zr_(1−x)Y_(x)O₂ F/C—Y₂O₃ F/C—Y₂O₃ F/C—Y₂O₃ Composition ss ss and ss Y₄Al₂O₉ Y₄Al₂O₉ and YAlO₃ Plasma Erosion Rate 0.3 1.44 0.3 0.1 0.1 0.2 (μm/hr) (CF₄/CHF₃) * All of the solid solution ceramic substrates were sintered using a pressureless sintering technique under a hydrogen protected atmosphere.

A review of the plasma erosion rate clearly shows the advantages of the solid solution yttrium oxide, zirconium oxide, aluminum oxide ceramics which have been described herein. We have demonstrated that it is possible to reduce the erosion rate of a ceramic material of this kind, while maintaining acceptable mechanical properties, which enable easier handling of the apparatus without risk of damage to the apparatus.

Combinations of yttrium oxide, zirconium oxide and aluminum oxide have been evaluated, and we have discovered that ceramic materials formed from starting compositions in which the Y₂O₃, yttrium oxide, molar concentration ranges from about 50 mole % to about 75 mole %; the ZrO₂, zirconium oxide, molar concentration ranges from about 10 mole % to about 30 mole %; and, the Al₂O₃, aluminum oxide, molar concentration ranges from about 10 mole % to about 30 mole %, provide excellent erosion resistance to halogen containing plasmas while providing advanced mechanical properties which enable handling of solid ceramic processing components with less concern about damage to a component. In many applications, a starting composition for the ceramic materials may be one in which Y₂O₃ molar concentration ranges from about 55 mole % to about 65 mole %, the ZrO₂ molar concentration ranges from about 10 mole % to about 25 mole % and the Al₂O₃ molar concentration ranges from about 10 mole % to about 20 mole %. When the erosion rate is of great concern, starting material concentration of the ceramic material may be one in which Y₂O₃ molar concentration ranges from about 55 mole % to about 65 mole %, the ZrO₂ molar concentration ranges from about 20 mole % to about 25 mole % and the Al₂O₃ molar concentration 5 mole % to about 10 mole %.

Starting material compositions of the kind described above may be used to form a ceramic coating over the surface of a variety of metal or ceramic substrates, including but not limited to aluminum, aluminum alloy, stainless steel, alumina, aluminum nitride, and quartz, using a technique well known in the art, such as plasma spray, for example and not by way of limitation. However, with the improved mechanical properties which have been obtained, it is recommended that solid ceramic apparatus components be used when possible, to prevent sudden failure of plasma resistance due to coating layer flaking off, or defects in the coating which appear as the coating thins, or the formation of metal contamination by mobile impurities from the underlying substrate which migrate into the coating.

The addition of a concentration of zirconium oxide, ranging from about 0.1 mole % to about 65 mole % to what was a pure yttrium oxide, provides a solid solution of yttrium oxide and zirconium oxide with the cubic yttria crystal structure or cubic fluorite-type crystal structure, where the cell parameter is smaller than that of the pure structure, due to the formation of yttrium vacancy/oxygen vacancy, respectively. The smaller cell parameter of the solid solution crystal structure improves the plasma resistance properties of the solid solution of zirconium oxide in yttrium oxide. For example, the erosion rate of a solid yttrium oxide ceramic in a CF₄/CHF₃ plasma of the kind used to etch a trench in a multilayered semiconductor substrate is about 0.3 μm/hr. The erosion rate of a solid solution ceramic of about 69 mole % yttrium oxide and about 31 mole % zirconium oxide is about 0.1 μm/hr, a 3 times slower etch rate than solid yttrium oxide. This unexpected decrease in etch rate extends the lifetime of a process chamber liner or an internal apparatus component within the process chamber, so that: the replacement frequency for such apparatus is reduced, reducing apparatus down time; the particle amount generated during a process is reduced, improving the product properties; the metal contamination generated during a process is reduced, advancing the product properties; and the overall will reduce the overall cost of the processing apparatus per wafer processed will be reduced, on the average.

While the 0.1 μm/hr erosion rate for the zirconium oxide-containing yttrium oxide solid solution is surprisingly better than that of yttrium oxide at 0.3 μm/hr, and considerably better than of a solid aluminum oxide ceramic at 1.44 μm/hr in the CF₄/CHF₃ plasma, the mechanical properties of the zirconium oxide-containing yttrium oxide solid solution illustrate that an improvement in flexural strength and fracture toughness would be helpful.

In one embodiment, the flexural strength and fracture toughness of the zirconium oxide-containing yttrium oxide solid solution are achieved, by adding various amounts of aluminum oxide to the formula for the solid solution ceramic to form an additional yttrium aluminate phase. The mixture of oxides was compacted by unidirectional mechanical pressing or cold isostatic pressing of a granular powder formed by spray drying, in combination with a typical content of binders. The green body was then pressureless sintered using techniques generally known in the art. The addition of 10 mole % to 30 mole % of alumina significantly improved the mechanical properties of the sintered ceramic composition in terms of flexural strength and fracture toughness. For example, the erosion rate of the ceramic containing 69 mole % yttrium oxide and 31 mole % zirconium oxide, after exposure to a plasma containing CF₄ and CHF₃, was about 0.1 μM/hr. For the ceramic containing about 14 mole % aluminum oxide, the erosion rate after exposure to the same plasma was also about 0.1 μm/hr. For the ceramic containing about 25 mole % aluminum oxide, the erosion rate after exposure to the same plasma was about 0.2 μM/hr. With respect to the mechanical properties, for example, an overall starting composition which is about 69 mole % yttrium oxide and about 31 mole % zirconium oxide, after sintering exhibits a flexural strength of about 137 Mpa, and a fracture toughness of 1.3 Mpa·m^(1/2), as discussed above. When the overall ceramic composition is about 63 mole % yttrium oxide, about 23 mole % zirconium oxide, and about 14 mole % aluminum oxide, after sintering the flexural strength is about 215 Mpa and the fracture toughness is about 1.6 Mpa·_(m) ^(1/2). When the overall ceramic composition is about 55 mole % yttrium oxide, about 20 mole % zirconium oxide, and about 25 mole % aluminum oxide, after sintering the flexural strength is about 172 Mpa and the fracture toughness is about 1.7 Mpa·m^(1/2). The relationship between aluminum oxide content, increase in flexural strength, and increase in erosion rate is not a linear relationship. However, one of skill in the art can optimize the formula with minimal experimentation, in view of the information provided herein.

As an alternative to adding aluminum oxide to a multi phase metal stable composition containing yttrium oxide and zirconium oxide is to add HfO₂, hafnium oxide; Sc₂O₃, scandium oxide; Nd₂O₃, neodymium oxide; Nb₂O₅, niobium oxide; Sm₂O₃, samarium oxide; Yb₂O₃, ytterbium oxide; Er₂O₃, erbium oxide; Ce₂O₃ (or CeO₂), cerium oxide, or combinations thereof. In the instance where these alternative compounds are used, the concentration of the alternative compound in the starting material formulation ranges from about 0.1 mole % to about 90 mole %. Typically the concentration used will range from about 10 mole % to about 30 mole %.

After mixing of at least one of the alternative oxides listed above with the Y₂O₃ and ZrO₂ powders used to form a solid solution, the combination of powders was compacted by unidirectionally mechanical pressing or cold isostatic pressing of the granular powder formed by spray drying with a typical content of binders. The green body was then pressureless sintered using techniques known in the art. Upon cooling of the sintered body, a single phase or two phase solid solution forms, where the solid solution is a “multi-element-doped” solid solution. One solid solution exhibits a cubic yttria crystal structure, and another solid solution exhibits the cubic fluorite-type crystal structure. The solid solution has excellent plasma resistance, typically better erosion resistance than that of the aluminum oxide-comprising solid solutions discussed herein. However, the mechanical properties of the yttria-zirconia-alumina system are somewhat better. All of these multi-doped solid solutions exhibit excellent plasma erosion resistance and improved mechanical properties in comparison with previously known yttrium oxide-zirconium oxide solid solutions.

Typical applications for a yttrium oxide-comprising substrate of the kind described herein include, but are not limited to components used internal to a plasma processing chamber, such as a lid, lid-liner, nozzle, gas distribution plate or shower head, electrostatic chuck components, shadow frame, substrate holding frame, processing kit, and chamber liner. All of these components are well known in the art to those who do plasma processing.

The above described exemplary embodiments are not intended to limit the scope of the present invention, as one skilled in the art can, in view of the present disclosure, expand such embodiments to correspond with the subject matter of the invention claimed below. 

We claim:
 1. A semiconductor processing apparatus comprising a substrate having at least one surface having a coating formed thereon, wherein the coating comprises a ceramic which is resistant to erosion by halogen-containing plasmas, wherein the ceramic comprises zirconium oxide at a molar concentration ranging from 96 mole % to 94 mole % and yttrium oxide at a molar concentration ranging from 4 mole % to 6 mole %, wherein the ceramic exhibits a flexural strength of from about 1100 MPa to about 1300 MPa, and wherein the ceramic has a mean grain size from about 0.5 μm to about 8.0 μm.
 2. The semiconductor processing apparatus in accordance with claim 1, wherein underlying the ceramic is a high purity aluminum alloy.
 3. The semiconductor processing apparatus in accordance with claim 1, wherein the apparatus is selected from the group consisting of a lid, a lid liner, a nozzle, a gas distribution plate, a shower head, an electrostatic chuck component, a shadow frame, a substrate holding frame, a processing kit, and a chamber liner.
 4. A semiconductor processing apparatus, the apparatus comprising a substrate having at least one surface having a coating formed thereon, wherein the coating comprises a ceramic which is resistant to erosion by halogen-containing plasmas, wherein the ceramic consists essentially of zirconium oxide at a molar concentration ranging from 96 mole % to 94 mole % and yttrium oxide at a molar concentration ranging from 4 mole % to 6 mole %, and wherein the ceramic has a mean grain size from about 0.5 μm to about 8.0 μm.
 5. The semiconductor processing apparatus in accordance with claim 4, wherein the ceramic exhibits a flexural strength of from about 1100 MPa to about 1300 MPa.
 6. The semiconductor processing apparatus in accordance with claim 1, wherein the ceramic exhibits a fracture toughness from about 10 MPa·m^(1/2) to about 12 MPa·m^(1/2).
 7. The semiconductor processing apparatus in accordance with claim 4, wherein the ceramic exhibits a fracture toughness from about 10 MPa·m^(1/2) to about 12 MPa·m^(1/2). 